Negative electrode material for secondary battery with non-aqueous electrolyte, method for manufacturing negative electrode material for secondary battery with non-aqueous electrolyte, and lithium ion secondary battery

ABSTRACT

The present invention is a negative electrode material for a secondary battery with a non-aqueous electrolyte comprising at least a silicon-silicon oxide composite and a carbon coating formed on a surface of the silicon-silicon oxide composite, wherein at least the silicon-silicon oxide composite is doped with lithium, and a ratio I(SiC)/I(Si) of a peak intensity I(SiC) attributable to SiC of 2θ=35.8±0.2° to a peak intensity I(Si) attributable to Si of 2θ=28.4±0.2° satisfies a relation of I(SiC)/I(Si)≦0.03, when x-ray diffraction using Cu—Kα ray. As a result, there is provided a negative electrode material for a secondary battery with a non-aqueous electrolyte that is superior in first efficiency and cycle durability to a conventional negative electrode material.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a negative electrode material for asecondary battery with a non-aqueous electrolyte, such as a lithium ionsecondary battery, to a method for manufacturing the same, and to alithium ion secondary battery by using the same, and the material iscomposed of a silicon-silicon oxide-lithium composite useful for thenegative electrode material for a secondary battery with a non-aqueouselectrolyte.

2. Description of the Related Art

Currently lithium ion secondary batteries are widely used for mobileelectronic devices, such as a mobile phone, a laptop computer, and thelike, because of high energy density. In recent years, with increasingawareness of environmental issues, an attempt to use this lithium ionsecondary battery as a power source for an electric automobile, which isan environmentally-friendly automobile, has become active.

However, the performance of a current lithium ion secondary battery isinsufficient for application to the electric automobile in terms ofcapacity and cycle durability. There has been accordingly advanceddevelopment of a next generation model of the lithium ion secondarybattery that has high capacity and is superior in cycle durability.

As one problem of the development of the next generation model of thelithium ion secondary battery, improvement in the performance of anegative electrode material is pointed out.

Currently carbon negative electrode materials are widely used. Thedevelopment by using a material other than carbon has also advanced tosharply enhance the performance, and a representative thereof is siliconoxide.

The silicon oxide has several times as much theoretical capacity ascarbon has, and there is thereby possibility that silicon oxide becomesan excellent negative electrode material.

There were, however, problems such as low first efficiency, lowelectronic conductivity, and low cycle durability at the beginning ofthe development, and various improvements have accordingly made so far.

Here, the “first efficiency” means a ratio of discharge capacity tocharge capacity in the first charge/discharge. As a result of the lowfirst efficiency, the energy density of the lithium ion secondarybattery decreases. It is considered that the low first efficiency ofsilicon oxide is caused by generating a lot of lithium compounds that donot contribute to the charge/discharge at the first charge.

As a method to solve this, there has been known a method of generatingthe above-described lithium compounds by making silicon oxide andlithium metal or a lithium compound (lithium oxide, lithium hydroxide,lithium hydride, organolithium, and the like) react in advance, beforethe first charge.

For example, Patent Literature 1 discloses use of a silicon oxide thatcan occlude and release lithium ions as a negative electrode activematerial, and a negative electrode material that satisfies a relation ofx>0 and 2>y>0 wherein a ratio of the number of atoms among silicon,lithium, and oxygen contained in the silicon oxide is represented by1:x:y.

As a method for manufacturing the above-described silicon oxide that isrepresented by a compositional formula of Li_(x)SiO_(y) and containslithium, there is disclosed a method in which a suboxide of siliconSiO_(y) that does not contain lithium is synthesized in advance, andlithium ions are occluded by an electrochemical reaction between theobtained suboxide of silicon SiO_(y) and lithium or a substancecontaining lithium. In addition, there is disclosed a method in which asimple substance of each of lithium and silicon, or a compound thereofare blended at a predetermined molar ratio, and it is heated under anon-oxidizing atmosphere or an oxygen-regulated atmosphere tosynthesize.

It describes that as a starting raw material, each of oxides andhydroxides, salts such as carbonates and nitrates, organolithiums, orthe like are exemplified, and although it is normally possible tosynthesize at a heating temperature of 400° C. or more, a temperature of400 to 800° C. is preferable, since a disproportionation reaction tosilicon and silicon dioxide may occur at a temperature of 800° C. ormore.

Moreover, Patent Literatures 2 to 4 describe that a chemical method oran electrochemical method is used as a method for preliminarilyinserting lithium before storing the negative electrode active materialin a battery container.

It describes that as the chemical method, a method of making thenegative electrode active material directly react with lithium metal, alithium alloy (lithium-aluminum alloy and the like), or a lithiumcompound (n-butyllithium, lithium hydride, lithium aluminum hydride, orthe like), and a lithium insertion reaction is preferably performed at atemperature of 25 to 80° C. in the chemical method. Moreover, itdiscloses, as the electrochemical method, a method of discharging, atopen system, oxidation reduction system in which the above-describednegative electrode active material is used for a positive electrodeactive material and a non-aqueous electrolyte containing lithium metal,a lithium alloy, or a lithium salt is used for a negative electrodeactive material, and a method of charging oxidation reduction systemthat is composed of a non-aqueous electrolyte that contains a transitionmetal oxide containing lithium, the negative electrode active material,and a lithium salt, as the positive electrode active material.

Moreover, Patent Literature 5 discloses powder of silicon oxidecontaining lithium represented by a general formula of SiLi_(x)O_(y), inwhich the ranges of x and y are 0<x<1.0 and 0<y<1.5, lithium is fused,and a part of the fused lithium is crystallized. It also discloses amethod for manufacturing the powder of the silicon oxide containinglithium, in which a blend of raw material powder that generates SiO gasand metallic lithium or a lithium compound is made to react by heatingunder an inert gas atmosphere or under reduced pressure at a temperatureof 800 to 1300° C.

It discloses that, at that time, silicon oxide (SiO_(z)) powder (0<z<2)and silicon dioxide powder can be used as the raw material powder thatgenerates SiO gas, and it is used after adding reduction powder(metallic silicon compounds, and powder containing carbon) as needed. Italso discloses that the metallic lithium and the lithium compounds arenot restricted in particular, and as the lithium compounds, for example,lithium oxide, lithium hydroxide, lithium carbonate, lithium nitrate,lithium silicate, hydrates thereof, or the like can be used, other thanthe metallic lithium.

On the other hand, when electronic conductivity is low, the capacity ofthe lithium ion secondary battery under high load decreases, andparticularly cycle durability decreases.

For improvement to enhance this electronic conductivity, PatentLiterature 6 discloses a negative electrode material having anelectronic conductive material layer formed on a surface of siliconoxide particles. It describes that the silicon oxide among them issilicon oxide having an elementary composition of Si and O, and ispreferably a suboxide of silicon represented by SiO_(x) (0<x<2), andthat it can be lithium silicate in which silicon oxide is doped with Li.It also describes that a carbon material is preferably used for aconductive material and it can be manufactured by using a CVD method, aliquid phase method, or a sintering method.

Moreover, as one improving method to enhance the cycle durability, thatis, to suppress an occurrence of a decrease in the capacity even whencharge/discharge are repeated, Patent Literature 7 discloses aconductive silicon composite in which a diffraction peak attributable toSi (111) is observed when x-ray diffraction, the size of silicon crystalobtained by the Scherrer method based on the half-width of a diffractionline thereof is 1 to 500 nm, and a surface of its particle is coatedwith carbon, the composite having a structure that crystallites ofsilicon are dispersed to a silicon compound, particularly, theconductive silicon composite in which the silicon compound is silicondioxide and at least a part of the surface thereof is adhered to carbon.

There is an example of a method for manufacturing this composite inwhich silicon oxide is subjected to disproportionation with an organicgas and/or vapor at a temperature of 900 to 1400° C., and carbon isdeposited by chemical vapor deposition treatment.

Moreover, for improvement in both of the first efficiency and cycledurability, Patent Literature 8 discloses a silicon-silicon oxidecomposite doped with lithium, the composite having a structure thatsilicon particles having a size of 0.5 to 50 nm are dispersed to siliconoxide in an atomic order and/or a crystallite state, particularly, aconductive silicon-silicon oxide-lithium composite in which the surfacethereof is coated with carbon at a coating amount of 5 to 50 mass % withrespect to an amount of the whole composite particles after surfacetreatment.

It describes a method for manufacturing this composite, the method inwhich silicon oxide is a lithium dopant and lithium metal and/or anorganolithium compound is used to dope with lithium at a temperature of1300° C. or less, and further a method in which a silicon-siliconoxide-lithium composite that is pulverized into a predetermined particlesize is subjected to heat CVD with an organic hydrocarbon gas and/orvapor at a temperature of 900 to 1400° C. and a carbon coating is formedat a coating amount of 5 to 50 mass % with respect to an amount of thewhole composite particles after surface treatment.

CITATION LIST Patent Literature

-   Patent Literature 1: Japanese Patent No. 2997741-   Patent Literature 2: Japanese Unexamined Patent publication (Kokai)    No. 8-102331-   Patent Literature 3: Japanese Unexamined Patent publication (Kokai)    No. 8-130011-   Patent Literature 4: Japanese Unexamined Patent publication (Kokai)    No. 8-130036-   Patent Literature 5: Japanese Unexamined Patent publication (Kokai)    No. 2003-160328-   Patent Literature 6: Japanese Unexamined Patent publication (Kokai)    No. 2002-42806-   Patent Literature 7: Japanese Patent No. 3952180-   Patent Literature 8: Japanese Unexamined Patent publication (Kokai)    No. 2007-294423

SUMMARY OF THE INVENTION

As described above, the silicon oxide negative electrode material hasbeen improved. However, even the most advanced art described in PatentLiterature 8 is still insufficient for practical use.

That is, the conductive silicon-silicon oxide-lithium compositemanufactured by the method described in Patent Literature 8 hasconsequently achieved extensive improvement in terms of the firstefficiency but the cycle durability thereof is inferior in comparisonwith a conductive silicon-silicon oxide composite that is not doped withlithium.

The present invention was accomplished in view of the aforementionedproblems, and it is an object of the present invention to provide asilicon oxide-based negative electrode material for a secondary batterywith a non-aqueous electrolyte, having superior first efficiency andcycle durability to a conventional negative electrode material, a methodfor manufacturing the same, and a lithium ion secondary battery usingthe same.

In order to accomplish the above object, the present invention providesa negative electrode material for a secondary battery with a non-aqueouselectrolyte including at least a silicon-silicon oxide composite and acarbon coating formed on a surface of the silicon-silicon oxidecomposite, wherein at least

the silicon-silicon oxide composite is doped with lithium, and a ratioI(SiC)/I(Si) of a peak intensity I(SiC) attributable to SiC of2θ=35.8±0.2° to a peak intensity I(Si) attributable to Si of2θ=28.4±0.2° satisfies a relation of I(SiC)/I(Si)≦0.03, when x-raydiffraction using Cu—Kα ray.

In this manner, the negative electrode material for a secondary batterywith a non-aqueous electrolyte, wherein, in the silicon-silicon oxidecomposite that is doped with lithium and has the carbon coating formedthereon, the ratio I(SiC)/I(Si) of the peak intensity I(SiC)attributable to SiC of 2θ=35.8±0.2° to the peak intensity I(Si)attributable to Si of 2θ=28.4±0.2° satisfies the relation ofI(SiC)/I(Si)≦0.03, when x-ray diffraction using Cu—Kα ray, can has asufficiently low amount of SiC at an interface between thesilicon-silicon oxide composite and the carbon coating, and thereby hasgood electronic conductivity and discharge capacity, and particularlygood cycle durability when used for a negative electrode material. Inaddition, since the negative electrode material is based on thesilicon-silicon oxide composite that is doped with lithium and has thecarbon coating formed thereon, it has higher capacity and superior in,particularly, the first efficiency as compared with a conventionalnegative electrode material.

In this case, a peak attributable to lithium aluminate can be furtherobserved in the negative electrode material for a secondary battery witha non-aqueous electrolyte, when the x-ray diffraction using Cu—Kα ray.

The above-described negative electrode material containing aluminum canalso has a sufficiently low amount of SiC at the interface between thesilicon-silicon oxide composite and the carbon coating, and thereby issuperior in, particularly, the cycle durability and the firstefficiency. As described later, lithium aluminum hydride containingaluminum is preferably used for doping with lithium.

Furthermore, the present invention provides a lithium ion secondarybattery having at least a positive electrode, a negative electrode, anda non-aqueous electrolyte having lithium ion conductivity, wherein thenegative electrode material for a secondary battery with a non-aqueouselectrolyte described in the present invention is used for the negativeelectrode.

As described above, the negative electrode material for a secondarybattery with a non-aqueous electrolyte according to the presentinvention enables good battery characteristics (the first efficiency andthe cycle durability) when used for a negative electrode of anon-aqueous electrolyte secondary battery. The lithium ion secondarybattery in which the negative electrode material for a secondary batterywith a non-aqueous electrolyte according to the present invention isused is therefore superior in the battery characteristics, particularly,the first efficiency and the cycle durability.

Furthermore, the present invention provides a method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte including at least coating a surface of powder composed ofat least one of silicon oxide and a silicon-silicon oxide composite withcarbon by heat CVD treatment, blending a lithium dopant with the powdercoated with carbon, and thereafter heating the powder coated with carbonto be doped with lithium.

In the case of coating with carbon by the heat CVD treatment afterdoping with lithium, silicon and carbon at the interface between thesilicon-silicon oxide composite and the carbon coating react toaccelerate generation of SIC due to the doping lithium, crystallizationof silicon contained in the silicon-silicon oxide composite isaccelerated, and thereby the electronic conductivity and cycledurability of the negative electrode material to be obtained in thiscase are not good. On the other hand, doping with lithium after thecoating of carbon as described above enables a sufficiently low amountof the generation of SiC at the interface between the silicon-siliconoxide composite and the carbon coating. In addition to this, it can besuppressed to excessively grow silicon crystal contained in thesilicon-silicon oxide composite, and the negative electrode material canbe manufactured, the material which enables good batterycharacteristics, such as cycle durability, when used for a negativeelectrode.

Moreover, when the silicon-silicon oxide composite is coated with carbonand doped with lithium, the capacity thereof can be improved incomparison with conventional methods, and the negative electrodematerial for a secondary battery with a non-aqueous electrolyte can bemanufactured which has improved conductivity and first efficiency.

In this case, lithium hydride and/or lithium aluminum hydride ispreferably used as the lithium dopant.

In this manner, when lithium hydride and/or lithium aluminum hydride isused as the lithium dopant, the reaction is milder in comparison withthe case of using lithium metal as the lithium dopant, and it can bedoped with lithium with readily controlling the temperature. Inaddition, silicon oxide can be more reduced in comparison with the caseof using a dopant containing oxygen, such as lithium hydroxide andlithium oxide, the negative electrode material having high dischargecapacity can be thereby manufactured, and it can be a method formanufacturing a high capacity negative electrode material suitable toindustrial mass production.

Moreover, the doping with lithium is preferably performed at atemperature equal to or lower than the temperature of the heat CVDtreatment.

In this manner, when the doping with lithium is performed at atemperature equal to or lower than the temperature of the heat CVDtreatment for coating with carbon, the acceleration of the generation ofSiC and of the crystallization of silicon at the interface between thesilicon-silicon oxide composite and the carbon coating can be surelysuppressed, and the negative electrode material superior in batterycharacteristics can be manufactured.

Moreover, the temperature of the doping with lithium is preferably 800°C. or less.

In this manner, when it is heated at a temperature of 800° C. or less tobe doped with lithium, SiC can be prevented from being generated, thesilicon crystal contained in the silicon-silicon oxide composite can beprevented from excessively growing, the discharge capacity and the cycledurability can be surely prevented from deteriorating, and the negativeelectrode material for a secondary battery with a non-aqueouselectrolyte having high capacity and high cycle durability can bemanufactured.

Moreover, the temperature of the heat CVD treatment is preferably 800°C. or more.

In this manner, when the temperature of the heat CVD treatment is 800°C. or more, crystallization of carbon contained in the carbon coatingand bonding of the carbon coating and the silicon-silicon oxidecomposite can be promoted, a high quality and fine carbon coating can beformed with high productivity, and the negative electrode material for asecondary battery with a non-aqueous electrolyte can be manufacturedwhich has higher capacity and is superior in the cycle durability.

As explained above, the present invention provides the siliconoxide-based negative electrode material for a secondary battery with anon-aqueous electrolyte, having superior first efficiency and cycledurability to a conventional negative electrode material, the method formanufacturing the same, and the lithium ion secondary battery using thesame.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a view showing an x-ray diffraction chart of the negativeelectrode material for a secondary battery with a non-aqueouselectrolyte in Example 1.

FIG. 2 is a view showing an x-ray diffraction chart of the negativeelectrode material for a secondary battery with a non-aqueouselectrolyte in Example 2.

FIG. 3 is a view showing an x-ray diffraction chart of the negativeelectrode material for a secondary battery with a non-aqueouselectrolyte in Comparative Example 2.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

Hereinafter, the present invention will be explained in more detail.

In order to achieve the above object, the present inventor hasrepeatedly keenly conducted studies on the problem of a conventionalnegative electrode material for a secondary battery with a non-aqueouselectrolyte and on the solution thereof.

The present inventor has thoroughly inspected the problem of the artdescribed in Patent Literature 8, which is the most advanced art, amongthem and discovered the cause of inferior electronic conductivity andcycle durability.

That is, the present inventor has found that in the conductivesilicon-silicon oxide-lithium composite manufactured by the methoddisclosed in Patent Literature 8, the carbon coating is apt to changeinto SiC and silicon is apt to crystallize when CVD treatment with highheat is performed after doping with lithium, and that this is caused bythe doping with lithium.

The mechanism is not quite clear. It can be, however, considered that apart of silicon oxide is reduced by lithium and becomes silicon duringthe doping with lithium by using lithium metal and/or an organolithiumcompound, this silicon is apt to change into SiC and to crystallize ascompared with silicon generated by the disproportionation, and causesdeterioration of the battery characteristics, particularly, the cycledurability and the discharge capacity, when used for a negativeelectrolyte.

The present inventor further has repeatedly keenly conducted studiesbased on the above result of the studies, and consequently found thatthe doping with lithium after coating with carbon, the surface of thesilicon oxide or the silicon-silicon oxide composite that is constitutedby silicon particles being dispersed to silicon oxide enables dopingwith lithium while suppressing progress of the crystallization ofsilicon and the change into SiC, and that use of this silicon-siliconoxide composite, as a negative electrode active material of thesecondary battery with a non-aqueous electrolyte, such as the lithiumion secondary battery, enables the secondary battery with a non-aqueouselectrolyte having higher capacity, higher first efficiency, andsuperior cycle durability in comparison with conventional ones to beobtained. The present inventor thereby brought the present invention tocompletion.

Hereinafter, the present invention will be explained in detail withreference to the drawings. However, the present invention is notrestricted thereto.

The negative electrode material for a secondary battery with anon-aqueous electrolyte according to the present invention comprises atleast the silicon-silicon oxide composite and the carbon coating formedon the surface of the silicon-silicon oxide composite.

In this negative electrode material, at least the silicon-silicon oxidecomposite is doped with lithium, and the ratio I(SiC)/I(Si) of the peakintensity I(SiC) attributable to SiC of 2θ=35.8±0.2° to the peakintensity I(Si) attributable to Si of 2θ=28.4±0.2° satisfies therelation of I(SiC)/I(Si)≦0.03, in the result of x-ray diffraction usingCu—Kα ray.

For example, it is a conductive silicon-silicon oxide-lithium compositehaving the carbon coating formed thereon. The negative electrodematerial is composed of a silicon-silicon oxide composite that has afine structure that silicon particles are dispersed to silicon oxideand/or lithium silicate in an atomic order and/or a crystallite stateand has superior conductivity due to the carbon coating, superior firstefficiency due to the doping with lithium, larger discharge capacitythan conventional ones, and good cycle durability. It is to be notedthat this dispersion structure can be observed by a transmissionelectron microscope.

Moreover, the ratio of the peak intensity I(SiC) attributable to SiC of2θ=35.8±0.2° to the peak intensity I(Si) attributable to Si of2θ=28.4±0.2° satisfies the relation of I(SiC)/I(Si)≦0.03, when x-raydiffraction using Cu—Kα ray.

This I(SiC)/I(Si) can be used as a criterion of the change of the carboncoating into SiC. In the case of I(SiC)/I(Si)>0.03, too many parts arechanged into SiC in the carbon coating, and this may make a negativeelectrode material inferior in electronic conductivity and dischargecapacity, because the generation of a large amount of SiC causes adecrease in the electronic conductivity of the interface and of thecarbon coating, the capacity of the lithium ion secondary battery underhigh load consequently decreases, and particularly the cycle durabilitydecreases. However, generating a very thin SiC layer at the interfacebetween the carbon coating and the silicon-silicon oxide composite isuseful for enhancing the adhesion strength of the coating.

The battery characteristics are therefore significantly deteriorated inthe case of I(SiC)/I(Si)>0.03, whereas it is sufficiently permissible tobe the amount of generated SiC under a condition of satisfying therelation of I(SiC)/I(Si)≦0.03, when x-ray diffraction using Cu—Kα ray.The negative electrode material for a secondary battery with anon-aqueous electrolyte according to the present invention accordinglysatisfies I(SiC)/I(Si)≦0.03.

In this case, the peak attributable to lithium aluminate can be furtherobserved in the negative electrode material for a secondary battery witha non-aqueous electrolyte according to the present invention, when thex-ray diffraction using Cu—Kα ray. Moreover, the peak attributable tolithium silicate can be also observed in the negative electrodematerial.

Here, lithium silicate means compounds represented by a general formulaof Li_(x)SiO_(y) (1≦x≦4, 2.5≦y≦4), and lithium aluminate means compoundsrepresented by a general formula of Li_(x)AlO_(y) (0.2≦x≦1, 1.6≦y≦2).

That is, the doping lithium can exist mainly in a state of lithiumsilicate and/or lithium aluminate in the negative electrode material fora secondary battery with a non-aqueous electrolyte, and thereby lithiumstably exists in the silicon-silicon oxide composite.

The negative electrode material according to the present invention canbe doped with lithium by using lithium aluminum hydride containingaluminum. This negative electrode material also has a sufficiently lowamount of SiC at the interface between the silicon-silicon oxidecomposite and the carbon coating and is superior in the cycle durabilityand the first efficiency.

Next, the method for manufacturing a negative electrode material for asecondary battery with a non-aqueous electrolyte according to thepresent invention will be explained in detail, but the method is ofcourse not restricted thereto.

First, powder is prepared which is composed of at least one of siliconoxide desirably being represented by a general formula of SiO_(x)(0.5≦x≦1.6), and the silicon-silicon oxide composite desirably havingthe structure that silicon particles are dispersed to silicon oxide inan atomic order and/or a crystallite state, the composite desirablyhaving a Si/O molar ratio of 1/0.5 to 1/1.6.

It is to be noted that this powder can be pulverized and classified in adesired particle size distribution.

The powder is coated with carbon by the heat CVD treatment to giveconductivity to the surface thereof.

It is to be noted that the time of the heat CVD treatment isappropriately set according to the relation of the carbon coatingamount. In the event that the prepared powder contains silicon oxide,silicon oxide changes into a silicon-silicon oxide composite due to theinfluence of the treatment heat.

In the event that particles aggregate during the treatment, theaggregation can be disintegrated with a ball mill and the like. When theaggregation is disintegrated, the heat CVD treatment can be performedagain by the same way as above.

Here, the temperature of the heat CVD treatment can be 800° C. or more.

For example, powder that is composed of at least one of silicon oxideand the silicon-silicon oxide composite can be subjected to carboncoating treatment by heating to a temperature of 800° C. or more anddesirably 1300° C. or less (more desirably 900 to 1300° C., further 900to 1200° C.), under an atmosphere containing at least an organic gasand/or vapor, by using a reactor that is heated at 800 to 1300° C. underinert gas flow.

As described above, when the temperature of the heat CVD treatment is800° C. or more, sufficient fusion between the carbon coating and thesilicon-silicon oxide composite, and sufficient alignment(crystallization) of carbon atom can be ensured. The negative electrodematerial for a secondary battery with a non-aqueous electrolyte that hashigher capacity and is superior in the cycle durability can be thereforeobtained. In addition, forming silicon crystallite does not take longtime, and it is efficient.

At this point in time, the silicon-silicon oxide composite powder havingthe carbon coating formed thereon has not been doped with lithium yet,in the present invention. The formation of SiC is thereby suppressedeven when the heat CVD treatment is performed at a high temperature of800° C. or more, particularly, 900° C. or more.

Moreover, a lithium dopant is blended with the powder coated withcarbon.

This blending is not restricted in particular as long as an apparatusthat enables uniform blending under a dry atmosphere is used, and atumbler mixer is exemplified as a small apparatus.

Specifically, a predetermined amount of the silicon-silicon oxidecomposite powder having the carbon coating formed thereon and of thelithium dopant is weighed out in a glove box under a dry air atmosphereto put into a stainless steel sealed container. They are rotated at roomtemperature for a predetermined time with them set to the tumbler mixer,and blended so as to be uniform.

Thereafter, the powder coated with carbon is heated to be doped withlithium.

Lithium hydride or lithium aluminum hydride can be used as the lithiumdopant. When lithium hydride is used, the first efficiency is higher incomparison with the case of using lithium aluminum hydride having thesame mass amount, and use of lithium hydride is thus better from theviewpoint of the battery characteristics. Moreover, lithium hydride maybe used together with lithium aluminum hydride. Commercial lithiumaluminum hydride as a reducing agent is circulated, and thus can beeasily obtained.

In the case of using, for example, metallic lithium having highreactivity as the lithium dopant, the reactivity of lithiating agent istoo high, and it is therefore necessary to perform the blending under aninert gas atmosphere, such as argon, in addition to under a dryatmosphere. On the other hand, in the case of using lithium hydrideand/or lithium aluminum hydride, the blending can be performed under adry atmosphere only, and is remarkably easy to handle.

Moreover, in the case of using metallic lithium and the like, a chainreaction occurs, and there is a high risk to create an ignited state. Inthe ignited state, there is a problem that a silicon crystal isexcessively grown and the capacity and the cycle durability therebydecrease, in some cases. In case of lithium hydride and/or lithiumaluminum hydride, the reaction proceeds slowly, and an increase intemperature due to reaction heat is several dozen degrees. The ignitedstate is not therefore created in this case, and the negative electrodematerial that has high capacity and is superior in the cycle durabilitycan be readily manufactured in an industrial scale.

Moreover, in the case of using a dopant containing oxygen, such aslithium hydride and lithium oxide, there is a risk of a decrease indischarge capacity, which is caused by an insufficient reduction amountof silicon oxide of the manufactured negative electrode material. On theother hand, in case of lithium hydride and/or lithium aluminum hydride,such a risk can be surely avoided, and the negative electrode materialhaving high capacity can be surely manufactured.

It is to be noted that when unreacted lithium hydride or lithiumaluminum hydride is left behind, it is undesirable in bothcharacteristic and safety aspects.

The lithiation reaction is solid-solid reaction between thesilicon-silicon oxide composite having the carbon coating formed thereonand the lithium dopant. However, since the rate of diffusion of lithiuminto a solid is generally low, it is difficult for lithium to penetratecompletely uniformly into the inside of the silicon-silicon oxidecomposite having the carbon coating formed thereon.

For safety sake, an additive amount of lithium is desirably equal to orless than an amount to supplement overall irreversible capacity (thedifference between the charge capacity and the discharge capacity at thefirst charge/discharge), that is, Li/O≦1.

The doping with lithium can be performed at a temperature equal to orlower than the temperature of the heat CVD treatment.

When the lithiation reaction treatment is performed at a temperatureequal to or lower than the temperature of the heat CVD treatment of thecarbon coating, the generation of SiC at the interface between thesilicon-silicon oxide composite and the carbon coating can be stronglysuppressed, the generation which is accelerate due to heating at thelithiation, and the negative electrode material superior in the batterycharacteristics, particularly the cycle durability can be therebyobtained.

The temperature of the doping with lithium can be 800° C. or less.

When the doping with lithium is performed at a temperature of 800° C. orless, the silicon crystal contained in the silicon-silicon oxidecomposite can be prevented from excessively growing, and thereby thedischarge capacity and the cycle durability can be surely prevented fromdeteriorating. That is, the negative electrode material for a secondarybattery with a non-aqueous electrolyte that has high capacity and issuperior in high cycle durability can be manufactured.

It is to be noted that temperature of the doping with lithium isdesirably 200° C. or more from the viewpoint of reactivity.

A reactor having a heating mechanism is preferably used for theabove-described lithiation reaction under an inert gas atmosphere, andthe detail thereof is not restricted in particular.

For example, continuous or batch-wise treatment can be performed.Specifically, a rotary furnace, a vertical moving bed reactor, a tunnelfurnace, a batch furnace, a rotary kiln, and the like may be selected,depending on a particular purpose. An electric tube furnace isexemplified as a small apparatus.

More specifically, the above-described blend is put into a quartz tubethrough which an argon gas flows, and heated with the electric tubefurnace to react for a predetermined time.

In the event that the heat CVD treatment is performed after the powdercomposed of silicon oxide or the silicon-silicon oxide composite isdoped with lithium, carbon reacts with silicon due to the influence ofthe doping lithium. The conductivity therefore decreases due to thegeneration of SiC, the cycle durability deteriorates due to excessivegrowth of the silicon crystal, and the battery characteristics thusdeteriorate. However, in the case of doping with lithium at a lowtemperature after coating with carbon as the present invention, thegeneration amount of SiC at the interface between the silicon-siliconoxide composite and the carbon coating and the growth of the siliconcrystal can be sufficiently suppressed, and the negative electrodematerial superior in the battery characteristics, such as the cycledurability, when used for a negative electrode can be obtained.

When the negative electrode material is used for a secondary batterywith a non-aqueous electrolyte, the negative electrode material for asecondary battery with a non-aqueous electrolyte can be thereforeobtained which has large discharge capacity and good cycle durability.In addition to this, low first efficiency, which is a fault of siliconoxide and the silicon-silicon oxide composite, is improved, in thenegative electrode material.

The negative electrode material for a secondary battery with anon-aqueous electrolyte obtained according to the present invention asabove can significantly contribute to the manufacture of an excellentnon-aqueous electrolyte secondary battery that has high capacity andgood first efficiency and is superior in the cycle performance,particularly a high performance lithium ion secondary battery, when usedfor the negative electrode active material of the non-aqueouselectrolyte secondary battery.

In this case, the obtained lithium ion secondary battery ischaracterized by the use of the above-described negative electrodeactive material, while the materials of the positive electrode, thenegative electrode, electrolyte, and separator, and the shape of thebattery are not restricted.

For example, the positive electrode active material to be used may betransition metal oxides, such as LiCoO₂, LiNiO₂, LiMn₂O₄, V₂O₅, MnO₂,TiS₂, and MOS₂, and chalcogen compounds.

For example, the electrolyte to be used may be lithium salts, such aslithium perchlorate, in a non-aqueous solution form. A non-aqueoussolvent to be used may be propylene carbonate, ethylene carbonate,dimethoxyethane, γ-butyrolactone and 2-methyltetrahydrofuran, alone orin admixture. Other various non-aqueous electrolytes and solidelectrolytes can be used.

It is to be noted that when a negative electrode is fabricated by usingthe above-described negative electrode material for a secondary batterywith a non-aqueous electrolyte, a conductive agent, such as graphite,can be added to the negative electrode active material.

In this case, the type of conductive agent is not restricted inparticular, as long as it is an electronically conductive material thatdoes not cause decomposition and alteration in the manufactured battery.Specifically, the usable conductive agent includes metals in powder orfiber form, such as Al, Ti, Fe, Ni, Cu, Zn, Ag, Sn and Si, naturalgraphite, synthetic graphite, various coke powders, mesa-phase carbon,vapor phase grown carbon fibers, pitch base carbon fibers, PAN basecarbon fibers, and graphite obtained by firing various resins.

With regard to an additive amount of the above-described conductiveagent, the amount of the conductive agent contained in a blend of thenegative electrode material for a secondary battery with a non-aqueouselectrolyte according to the present invention and the conductive agentis desirably 1 to 60 mass % (more desirably 5 to 60 mass %, particularly10 to 50 mass %, more particularly 20 to 50 mass %).

When the additive amount of the conductive agent is 1 mass % or more, arisk of not being able to withstand expansion and contraction associatedwith charge/discharge can be avoided. In addition, when it is 60 mass %or less, a risk of a decrease in charge/discharge capacity can bereduced as much as possible.

When a carbon-based conductive agent is used for the negative electrode,the total amount of carbon in the negative electrode active material isdesirably 5 to 90 mass % (more desirably 25 to 90 mass %, particularly30 to 50 mass %).

When the total amount is 5 mass % or more, it can withstand theexpansion and contraction associated with charge/discharge. In addition,when the total amount is 90 mass % or less, the charge/dischargecapacity does not decrease.

EXAMPLES

Hereinafter, the present invention will be explained in detail byshowing Examples and Comparative Examples. However, the presentinvention is not restricted to Examples below.

It is to be noted that in Examples below, “%” indicate “mass %”, and anaverage particle size is measured as a cumulative weight average value(or median diameter) D₅₀ upon measurement of particle size distributionby laser diffractometry. The size of silicon crystal is a size of acrystallite of Si (111) face obtained by the Scherrer method from dataof the x-ray diffraction using Cu—Kα ray.

Example 1

Metallic silicon and silicon dioxide were blended at a molar ratio of1:1, and reacted at 1400° C. under a reduced pressure of 100 Pa togenerate a silicon oxide gas. The gas was cooled at 900° C. under areduced pressure of 50 Pa to precipitate, and a product in mass form wasconsequently obtained. The product was pulverized with a dry-type ballmill to obtain powder having an average particle size of 5 μm.

Chemical analysis revealed that the composition of this powder wasSiO_(0.95), the structure that silicon particles were dispersed tosilicon oxide in an atomic order and/or a crystallite state was observedwith a transmission electron microscope, and the powder was thussilicon-silicon oxide composite. The size of silicon crystal of thissilicon-silicon oxide composite was 4 nm.

The powder of the silicon-silicon oxide composite was subjected to theheat CVD treatment by using a raw material of a methane gas at 1100° C.under a reduced pressure of 1000 Pa for 5 hours to coat the surface ofthe powder with carbon. As a result, the carbon coating amount was 5% ofthe whole powder including the coating.

Next, 2.7 g powder of lithium hydride (reagent made by Wako PureChemical Industries, Ltd) was put into a porcelain mortar having aninternal volume of 500 ml and pulverized in a glove box under a dry airatmosphere. Thereafter, 28.4 g silicon-silicon oxide composite powderhaving the carbon coating formed thereon was added thereto (lithiumhydride:the silicon-silicon oxide composite (except carbon)=1:10 (a massratio)), and they were stirred and blended so as to be sufficientlyuniform.

The blend of 29 g was transferred to a 70 ml alumina boat and the boatwas carefully placed at the center of a furnace tube of an electric tubefurnace provided with an alumina furnace tube having an inner diameterof 50 mm. It was heated up to 600° C. at 5° C. every minute whilepassing an argon gas at 2 liters every minute, and was cooled afterholding of 1 hour.

The doping amount of lithium of the negative electrode material for asecondary battery with a non-aqueous electrolyte obtained as above was8%. The structure that silicon particles were dispersed to silicon oxidein an atomic order and/or a crystallite state was observed with atransmission electron microscope.

Moreover, the peaks attributable to silicon and lithium silicate wereobserved when the x-ray diffraction using Cu—Kα ray. It was confirmedthat the size of silicon crystal was 10 nm, and thus the growth of thesilicon crystal was suppressed. It was further confirmed that the ratioof the peak intensity I(SiC) attributable to SiC of 2θ=35.8±0.2° to thepeak intensity I(Si) attributable to Si of 2θ=28.4±0.2° satisfied arelation of I(SiC)/I(Si)=0, when x-ray diffraction using Cu—Kα ray, andthus the generation of SiC was suppressed. The x-ray diffraction chartthereof is shown in FIG. 1.

Example 2

Except that lithium aluminum hydride was used as the lithium dopant inExample 1, the negative electrode material for a secondary battery witha non-aqueous electrolyte was manufactured in the same conditions asExample 1, and the same evaluation was carried out.

As a result, the doping amount of lithium was 2%. The structure thatsilicon particles were dispersed to silicon oxide in an atomic orderand/or a crystallite state was observed with a transmission electronmicroscope.

Moreover, it was confirmed that the peaks attributable to silicon,lithium silicate, and lithium aluminate were observed when the x-raydiffraction using Cu—Kα ray, the size of silicon crystal was 10 nm, andthus the growth of the silicon crystal was suppressed. It was furtherconfirmed that the ratio satisfied a relation of I(SiC)/I(Si)=0, andthus the generation of SiC was suppressed. The x-ray diffraction chartthereof is shown in FIG. 2.

Example 3

Powder of a silicon-silicon oxide composite having a silicon crystalsize of 4 nm was obtained by the same method as Example 1.

Except that the temperature of the heat CVD treatment was 1300° C. andthe treatment time thereof was 1 hour, this powder of thesilicon-silicon oxide composite was subjected to the heat CVD treatmentin the same condition as Example 1, and the silicon-silicon oxidecomposite powder having the carbon coating formed thereon at a carboncoating amount of 5% was consequently obtained.

Next, the silicon-silicon oxide composite powder having the carboncoating formed thereon was reacted with lithium hydride in the samecondition as Example 1.

The structure that silicon particles were dispersed to silicon oxide inan atomic order and/or a crystallite state was observed with atransmission electron microscope, in the negative electrode material fora secondary battery with a non-aqueous electrolyte obtained as above.

Moreover, it was confirmed that the peaks attributable to silicon andlithium silicate were observed when the x-ray diffraction using Cu—Kαray, the size of silicon crystal was 28 nm, and thus the growth of thesilicon crystal was suppressed. It was further confirmed that the ratiosatisfied a relation of I(SiC)/I(Si)=0.026, and thus the generation ofSiC was suppressed.

Example 4

Powder of a silicon-silicon oxide composite having a silicon crystalsize of 4 nm was obtained by the same method as Example 1.

Except that the treatment time of the heat CVD treatment was 63 hours,this powder of the silicon-silicon oxide composite was subjected to theheat CVD treatment in the same condition as Example 1, and thesilicon-silicon oxide composite powder having the carbon coating formedthereon at a carbon coating amount of 40% was consequently obtained.

Next, the silicon-silicon oxide composite powder having the carboncoating formed thereon was reacted with lithium hydride in the samecondition as Example 1.

The structure that silicon particles were dispersed to silicon oxide inan atomic order and/or a crystallite state was observed with atransmission electron microscope, in the negative electrode material fora secondary battery with a non-aqueous electrolyte obtained as above.

Moreover, it was confirmed that the peaks attributable to silicon andlithium silicate were observed when the x-ray diffraction using Cu—Kαray, the size of silicon crystal was 13 nm, and thus the growth of thesilicon crystal was suppressed. It was further confirmed that the ratiosatisfied a relation of I(SiC)/I(Si)=0.011, and thus the generation ofSiC was suppressed.

Comparative Example 1

Powder of a silicon-silicon oxide composite having a silicon crystalsize of 4 nm was obtained by the same method as Example 1.

This powder of the silicon-silicon oxide composite was subjected to theheat CVD treatment in the same condition as Example 1, and thesilicon-silicon oxide composite powder having the carbon coating formedthereon at a carbon coating amount of 5% was consequently obtained. Thesize of silicon crystal of the powder was 7 nm.

The powder was used for a negative electrode material for a secondarybattery with a non-aqueous electrolyte without doping with lithium.

Comparative Example 2

Except that, in Example 1, the order of a heat CVD process (at atemperature of 1100° C., for 5 hours) and a process of doping withlithium (use of lithium hydroxide, lithium hydroxide:the silicon-siliconoxide composite=1:10, a holing time of 1 hour at a temperature of 600°C.) was reversed, a negative electrode material for a secondary batterywith a non-aqueous electrolyte was manufactured in the same condition asExample 1, and the same evaluation was carried out.

It was revealed that the size of silicon crystal was 37 nm from theresult of the x-ray diffraction using Cu—Kα ray of the obtained negativeelectrode material for a secondary battery with a non-aqueouselectrolyte, and thus the growth of silicon crystal was considerablyaccelerated due to lithium.

It was confirmed that the ratio satisfied a relation ofI(SiC)/I(Si)=0.034, and thus SiC was largely generated. The x-raydiffraction chart thereof is shown in FIG. 3.

Comparative Example 3, 4, and 5

Except that, in Comparative Example 2, the temperature and the time ofthe heat CVD treatment process were 1300° C. and 1 hour (ComparativeExample 3), 1300° C. and 10 hours (Comparative Example 4), 800° C. and120 hours (Comparative Example 5), respectively, a negative electrodematerial for a secondary battery with a non-aqueous electrolyte wasmanufactured in the same condition as Comparative Example 2, and thesame evaluation was carried out.

As a result, it was revealed that the sizes of silicon crystal were 45nm (Comparative Example 3), 60 nm (Comparative Example 4), and 35 nm(Comparative Example 5), respectively, and thus the growth of siliconcrystal was considerably accelerated due to lithium as with ComparativeExample 2.

Moreover, it was confirmed that the ratio satisfied a relation ofI(SiC)/I(Si)=0.041 (Comparative Example 3), I(SiC)/I(Si)=0.050(Comparative Example 4), I(SiC)/I(Si)=0.034 (Comparative Example 5),respectively, and thus SiC was largely generated.

Comparative Example 6

Except for lithium hydroxide:the silicon-silicon oxide composite (exceptcarbon)=1:2000 (a mass ratio) in Comparative Example 2, a negativeelectrode material for a secondary battery with a non-aqueouselectrolyte was manufactured in the same condition as ComparativeExample 2, and the same evaluation was carried out.

As a result, it was revealed that the size of silicon crystal was 34 nm,and the growth of silicon crystal was accelerated as with ComparativeExample 2 to 5, despite a small doping amount of lithium.

Moreover, it was confirmed that the ratio satisfied a relation ofI(SiC)/I(Si)=0.032, and thus SiC was largely generated.

(Battery Evaluation)

The evaluation as the negative electrode active material for a lithiumion secondary battery was carried out by the following method/procedurewhich was common to all Examples and Comparative Examples.

A blend was first produced by adding flake synthetic graphite powder(average particle diameter D₅₀=5 μm) to the obtained negative electrodematerial for a secondary battery with a non-aqueous electrolyte of 20 gin such amounts that the total of carbon in flake synthetic graphite andthe carbon coating formed on the negative electrode material for asecondary battery with a non-aqueous electrolyte was 42%.

Binder KSC-4011 made by Shin-Etsu Chemical Co., Ltd. was added in anamount of 10% as solids to the blend to form a slurry at the temperaturenot exceeding 20° C. N-methylpyrrolidone was further added for viscosityadjustment. This slurry was speedily coated onto a copper foil having athickness of 20 μm and dried at 120° C. for 1 hour. An electrode wasthereafter formed by pressing with a roller press and finally punchedout so as to have a size of 2 cm² as the negative electrode. At thispoint in time, the mass of the negative electrode was measured tocalculate the mass of the negative electrode material by subtracting themass of the copper foil, flake synthetic graphite powder, and the bindertherefrom.

To evaluate the charge/discharge characteristics of the obtainednegative electrode, a lithium-ion secondary battery for evaluation wasfabricated using a lithium foil as a counter electrode; using, as anon-aqueous electrolyte, a non-aqueous electrolyte solution obtained bydissolving lithium hexafluorophosphate in a 1/1 (a volume ratio) mixtureof ethylene carbonate and 1,2-dimethoxyethane at a concentration of 1mol/L; and using a polyethylene microporous film having a thickness of30 μm as a separator.

The fabricated lithium-ion secondary battery was allowed to standovernight at room temperature. Thereafter, with a secondary batterycharge/discharge test apparatus (made by Nagano, Co., Ltd.), the batteryfor evaluation was charged at a constant current of 1.5 mA until thetest cell voltage reached 5 mV at room temperature. After the voltagereached 5 mV, the battery was charged at a reduced current so that thecell voltage was maintained at 5 mV. When the current value haddecreased below 200 μA, the charging was terminated. The battery wasdischarged at a constant current of 0.6 mA, and the discharging wasterminated when the cell voltage reached 2.0 V.

The charge/discharge capacity per unit mass of the negative electrodematerial was calculated by subtracting the charge/discharge capacity ofthe flake synthetic graphite powder from the above-obtainedcharge/discharge capacity.

capacity per mass (mAh/g)=discharge capacity of negative electrodematerial (mAh)/mass of negative electrode material (g)

first efficiency (%)=discharge capacity of negative electrode material(mAh)/charge capacity of negative electrode material (mAh)×100

The charge/discharge test of the lithium-ion secondary battery forevaluation was carried out 50 times by repeating the charge/dischargetest as above, to evaluate the cycle durability.

capacity retention ratio (o)=discharge capacity of negative electrodematerial after 50 cycles (mAh)/first discharge capacity of negativeelectrode material (mAh)×100

Table 1 shows the result of evaluating the negative electrode materialfor a secondary battery with a non-aqueous electrolyte in Examples 1 to4 and Comparative Examples 1 to 6 by the above-described method.

TABLE 1 FIRST CAPACITY CAPACITY EFFI- RETEN- PER MASS CIENCY TION(mAh/g) (%) RATIO (%) RESULT EXAMPLE 1 1370 85 89 GOOD EXAMPLE 2 1430 7689 GOOD EXAMPLE 3 1400 86 81 GOOD EXAMPLE 4 870 85 93 GOOD COM- 1500 6690 LOW FIRST PARATIVE EFFICIENCY EXAMPLE 1 COM- 1320 84 35 INFERIORPARATIVE CYCLE EXAMPLE 2 DURABILITY COM- 1310 83 30 INFERIOR PARATIVECYCLE EXAMPLE 3 DURABILITY COM- 1300 80 18 INFERIOR PARATIVE CYCLEEXAMPLE 4 DURABILITY COM- 1330 84 36 INFERIOR PARATIVE CYCLE EXAMPLE 5DURABILITY COM- 1400 69 39 INFERIOR PARATIVE CYCLE EXAMPLE 6 DURABILITY

As shown in Table 1, it was revealed that the cases of the negativeelectrode materials in Examples 1 to 4, where the doping with lithiumwas performed after forming the carbon coating and a relation ofI(SiC)/I(Si)≦0.03 was satisfied, showed a good value of each of thecapacity per mass, the first efficiency, the capacity retention ratioafter 50 cycles (cycle durability).

On the other hand, it was revealed that the case of Comparative Example1, where the doping with lithium was not performed, showed inferiorfirst efficiency, and that the cases of Comparative Examples 2 to 6,where the value of I(SiC)/I(Si) exceeded 0.03, showed inferior cycledurability and a large amount of SiC generation, whereas the capacityper mass and the first efficiency had no problem, and thus hadcharacteristic problems for the negative electrode material.

As described above, it is revealed that when the doping with lithium isperformed after forming the carbon coating, the generation of SiC issuppressed so that the relation of I(SiC)/I(Si)≦0.03 is satisfied, evenwhen the temperature of the heat CVD treatment is high and the dopingamount of lithium is large, and the battery characteristics become good.

On the other hand, it is revealed that when the heat CVD treatment isperformed after doping with lithium, SiC is largely generated so thatthe value of I(SiC)/I(Si) exceeds 0.03, even when the temperature of theheat CVD treatment is low and the doping amount of lithium is small, andthe battery characteristics do not become good.

It is to be noted that the present invention is not restricted to theforegoing embodiment. The embodiment is just an exemplification, and anyexamples that have substantially the same feature and demonstrate thesame functions and effects as those in the technical concept describedin claims of the present invention are included in the technical scopeof the present invention.

1. A negative electrode material for a secondary battery with anon-aqueous electrolyte comprising at least a silicon-silicon oxidecomposite and a carbon coating formed on a surface of thesilicon-silicon oxide composite, wherein at least the silicon-siliconoxide composite is doped with lithium, and a ratio I(SiC)/I(Si) of apeak intensity I(SiC) attributable to SiC of 2θ=35.8±0.2° to a peakintensity I(Si) attributable to Si of 2θ=28.4±0.2° satisfies a relationof I(SiC)/I(Si)≦0.03, when x-ray diffraction using Cu—Kα ray.
 2. Thenegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 1, wherein a peak attributable to lithiumaluminate is further observed in the negative electrode material for asecondary battery with a non-aqueous electrolyte, when the x-raydiffraction using Cu—Kα ray.
 3. A lithium ion secondary battery havingat least a positive electrode, a negative electrode, and a non-aqueouselectrolyte having lithium ion conductivity, wherein the negativeelectrode material for a secondary battery with a non-aqueouselectrolyte according to claim 1 is used for the negative electrode. 4.A lithium ion secondary battery having at least a positive electrode, anegative electrode, and a non-aqueous electrolyte having lithium ionconductivity, wherein the negative electrode material for a secondarybattery with a non-aqueous electrolyte according to claim 2 is used forthe negative electrode.
 5. A method for manufacturing a negativeelectrode material for a secondary battery with a non-aqueouselectrolyte comprising at least coating a surface of powder composed ofat least one of silicon oxide and a silicon-silicon oxide composite withcarbon by heat CVD treatment, blending a lithium dopant with the powdercoated with carbon, and thereafter heating the powder coated with carbonto be doped with lithium.
 6. The method for manufacturing a negativeelectrode material for a secondary battery with a non-aqueouselectrolyte according to claim 5, wherein lithium hydride and/or lithiumaluminum hydride is used as the lithium dopant.
 7. The method formanufacturing a negative electrode material for a secondary battery witha non-aqueous electrolyte according to claim 5, wherein the doping withlithium is performed at a temperature equal to or lower than atemperature of the heat CVD treatment.
 8. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 6, wherein the doping with lithium isperformed at a temperature equal to or lower than a temperature of theheat CVD treatment.
 9. The method for manufacturing a negative electrodematerial for a secondary battery with a non-aqueous electrolyteaccording to claim 5, wherein the temperature of the doping with lithiumis 800° C. or less.
 10. The method for manufacturing a negativeelectrode material for a secondary battery with a non-aqueouselectrolyte according to claim 6, wherein the temperature of the dopingwith lithium is 800° C. or less.
 11. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 7, wherein the temperature of the dopingwith lithium is 800° C. or less.
 12. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 8, wherein the temperature of the dopingwith lithium is 800° C. or less.
 13. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 5, wherein the temperature of the heatCVD treatment is 800° C. or more.
 14. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 6, wherein the temperature of the heatCVD treatment is 800° C. or more.
 15. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 7, wherein the temperature of the heatCVD treatment is 800° C. or more.
 16. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 8, wherein the temperature of the heatCVD treatment is 800° C. or more.
 17. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 9, wherein the temperature of the heatCVD treatment is 800° C. or more.
 18. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 10, wherein the temperature of the heatCVD treatment is 800° C. or more.
 19. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 11, wherein the temperature of the heatCVD treatment is 800° C. or more.
 20. The method for manufacturing anegative electrode material for a secondary battery with a non-aqueouselectrolyte according to claim 12, wherein the temperature of the heatCVD treatment is 800° C. or more.